JPS6074104A - Digital magnetic head - Google Patents

Abstract

PURPOSE:To raise a magnetic permeability in a high frequency area, and to improve a symmetricalness of a peak shift by forming a part of a magnetic circuit by a composite material obtained by a dispersing uniformly and three-dimensionally the second phase particles in a super-quenching alloy matrix consisting of amorphous and crystalline materials, etc. CONSTITUTION:An alloy base material 11 of a molten state is formed and injected into a mold 3 by melting mutually constituting metals Co, Fe, Si and B in a prescribed ratio in a vacuum high frequency melting furnace 2. Subsequently, a WC fine powder 4 is jetted by a necessary quantity toward a mold injecting flow of an alloy base material 1 by a high pressure argon gas from a bomb 6. In this way, an ingot 8 consisting of a Co-Fe-Si-B compound alloy in which the WC fine powder has been dispersed uniformly is obtained. Next, this ingot is put into a heat resisting pipe 7 made of a quartz glass, the inside of the pipe is replaced enough with gaseous argon 9, and thereafter, it is melted in a high frequency melting furnace 10. Subsequently, a piston 11 is operated and the lower end nozzle of the heat resisting pipe 7 is made to approach as near as possible the joining part of two rollers 12, 12 rotating at a high speed, an argon gas pressure in the heat resisting pipe is raised suddenly, the ingot 8 is supplied to the joining part of the rolls 12, 12 as a uniform continuous jet, and a ribbon-shaped core material 13 having specified width and thickness is obtained.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a digital magnetic head, and particularly to a core material constituting a magnetic circuit thereof.

A digital read-after-write magnetic head is usually installed in computer peripheral equipment, etc., and has multiple pairs of write and read gaps for multi-channel use. When the magnetic tape runs over this magnetic head, digital signals are recorded on the tape in the writing gap.
Immediately thereafter, the tape is passed over the read gap to read out the signal and check the accuracy of the write signal.

Writing and reading of this digital magnetic head is done in a high frequency range of about 1 to 3 MHz due to the high recording density, so the core material used in the magnetic head is made of materials with particularly high magnetic permeability and low saturation magnetic flux density. things are required. By the way, as a conventional core material, permalloy processed to a thin thickness of about 25 to 50 μm is used.
Fix the concubine.

was. However, this thin plate-like permalloy is
- When internal stress is generated by mechanical tightening, the magnetic permeability decreases to about 600-ROO at 11vl)lz. If you use a core material with poor frequency characteristics like this,
A phase shift Jl occurs in the signal waveform in the high frequency region, causing the signal waveform to become symmetrical or asymmetrical, resulting in a decrease in the reliability of computer peripheral equipment.

The present inventors used a liquid quenching method, which is conventionally known as the ffu production method for ultra-quenched alloys, to obtain a τ second phase of 1::1. This new composite material selectively combines the excellent properties and functions of both their constituent materials (quenched magnetic alloys and second phase particles). It has been found that this material is very suitable as a material for digital magnetic heads.

That is, the present invention provides a composite material in which at least one second phase particle is uniformly dispersed three-dimensionally in an ultra-quenched alloy matrix consisting of an amorphous, crystalline, or mixed phase thereof. It is characterized in that it constitutes a part of the

In the present invention, the alloy matrix constituting the ultra-quenched alloy 71-ricks includes, for example, a cobalt-based alloy such as a cobalt-iron alloy containing cobal 1- as a main component, an iron-silicon-boron alloy containing iron as a main component, and an iron-silicon-boron alloy containing iron as a main component. Iron-based alloys such as iron-molybdenum alloys, nickel-based alloys such as nickel-silicon-boron alloys whose main component is nickel, or copper-zirconium alloys.

Various types of alloys such as zirconium-niobium alloys are used.

In the present invention, the second phase particles include 1. For example, C1WC
, T i C, N l) Carbon or carbide such as C.

Nitride such as NbN and TaN, Cr: 03, CeO
2.

MgO, Zr01z, Y:○q, WO3, Th'
O: .

AQ=OB, Fe:=○−+, ZnO, 5i
C) Infusions such as z, borides such as BN, silicates such as SiC, gold scraps such as Ti, Fe, Mo, W, etc. are used.

Next, an example of manufacturing the core material according to the present invention will be described. Figures 1 and 2 are principle explanatory diagrams for explaining the first manufacturing example, Figure 1 is a diagram for explaining the process of making an ingot, and Figure 2 is a diagram for explaining the process of making an ingot. 6. In FIG. 1, the alloy matrix l constituting the ultra-quenched alloy matrix is heated and melted in a vacuum high-frequency melting furnace 2, Injected into 3. On the other hand, the second phase particles 4 are forcibly sprayed and added to the molten alloy base material 1 which is being injected into the mold 3 by the plasma spraying powder feeder 5, and are cooled and solidified as they are to form the second phase particles 4. -Rgots 1- are obtained in which a uniform fraction of is retained. For spraying and dispersing the second phase particles 4, the spray IA! is made of an inert gas such as Alcon gas filled in the cylinder 6! Four bodies are used.

In order to avoid deterioration of the alloy base material 1 during injection dispersion, an inert gas such as argon gas is preferably used as the injection medium. As a powder feeder for supplying the second phase particles 4, the second phase powder 4 can be supplied uniformly at all times, injection conditions such as injection pressure can be adjusted relatively easily, and the nozzle has excellent heat resistance. For this reason, a powder feeder for plasma spraying is suitable.

-C is a method of creating a ribbon-like material using an ultra-quenching method.
There are single roll method, double roll method and centrifugal method. These ultra-quenching methods are capable of producing metastable materials that are not in the equilibrium phase diagram, such as amorphous phases and non-equilibrium crystalline layers, or crystallized rWr materials by controlling the selection of alloy composition or quenching conditions such as quenching rate. Phases etc. can be obtained.

FIG. 2 shows the manufacturing process for creating a ribbon-shaped core material by the twin roll method. In a heat-resistant tube 7 made of quartz glass with a nozzle at the lower end, the injector 1-8 in which the second phase particles are uniformly dispersed is placed, and the inert gas 9τ-4-41 is filled with argon gas inside the tube. A oligo-solid oil melting furnace 10 is installed in the first section of the trade section, and the ingots 1-8 are remelted by this melting furnace 10 to the extent that the second phase particles are not melted. be done. Then piston 1
1 to move the nozzle tip of the heat-resistant tube 7 as close as possible to the joint of the two rolls 12 and 12 rotating at high speed, and rapidly increase the gas pressure inside the heat-resistant tube 7. .

The remelted ingot 8 is gradually fed from a nozzle as a uniform continuous jet to the joint of the rolls 2 and 12 due to pressure. Since the rolls 12.12 are rotating at high speed and are pressed against each other, when the molten metal is ejected, it is instantaneously solidified in a cold JIP to obtain a continuous ribbon-shaped core material 13. 6 Fig. 3 is an enlarged cross-sectional view of this core 4; J13, in which extremely fine +t
The second phase particles 4 are three-dimensionally uniformly dispersed. The thickness and width of core +113 are as per roll 1.
The circumferential speed and contact force of 2, the temperature of the melt and j7
It is possible to make adjustments by varying the speed, etc.

The twin roll method explained using Fig. 2 has the advantage that the thickness of the core material obtained is uniform, the surface roughness is small on both sides, and relatively thick core materials can be manufactured easily. There is.

Although a twin roll method was used in this production example, a single roll method may be applied instead.

FIG. 4 is a principle explanatory diagram for explaining a second manufacturing example of the core material according to the present invention.

A heat-resistant tube 7 made of quartz glass having a nozzle at the lower end,
An ingot of the alloy base material 1 constituting the super-quenched alloy matrix is placed, and the inside of the tube is sufficiently replaced with an inert gas 9 such as argon gas. A high-frequency melting furnace 4 is installed around the outer periphery of the heat-resistant tube 7, and the ingot of the alloy base material 1 is melted by the melting furnace 4 to such an extent that second phase particles 4, which will be described later, are not melted. Thereafter, the piston 11 is actuated to bring the nozzle tip of the heat-resistant tube 7 as close as possible to the upper peripheral surface of the roller 6 that is rotating at high speed, and the inert gas pressure inside the heat-resistant tube 7 is rapidly increased. The molten alloy base material J is supplied to the circumferential surface of the roll 6 from a nozzle as a thin, uniform, continuous jet due to the pressure increase.

With respect to the jet flow of the alloy base material X from the heat-resistant tube 7.

The second phase particles 4 are forcibly added by injection together with a III injection medium such as argon gas by a plasma spray feeder 5. The alloy base material 1 in the molten state to which the second phase particles 4 have been added is stretched on the a-rule 12 and rapidly solidified in the I2 to obtain a continuous ribbon-like a4A+3. It will be done.

Core material thus obtained 1. :3 #J 1M3 rapidly solidified alloy 71.Similar to the one shown in Figure 3. The extremely fine second phase particles 1 are uniformly dispersed in the third dimension in I4.

The single roll method explained using FIG. 11 has a ratio of I! '2j
+It has the advantage that it is easy to obtain a wide and thin film. In this production example, the jii[4-l method was used, but it is also possible to use the twinronyl method instead.

FIG. 5 is a diagram illustrating the principle of a third manufacturing example of the core product according to the present invention.

An ingot of the alloy base material I constituting the ultra-quenched alloy 71 is placed in a heat-resistant tube 7 made of quartz glass having a nozzle at the lower end, and the inside of the tube is sufficiently replaced with an inert gas 9 such as argon gas. A high-frequency melting furnace 10 is installed on the outer periphery of the heat-resistant tube 7, and the ingot 1- of the alloy base material 1 is melted by the melting furnace 10 to the extent that fJ52 phase particles 4, which will be described later, are not melted.
melted. Thereafter, the piston 11 is operated to rapidly increase the inert gas pressure in the heat-resistant tube 7, and mml of the alloy base material 1 is poured into the molten metal reservoir 15 disposed below.

The second phase particles 4 are forcibly added to the jet stream of the alloy base material 1 from the heat-resistant tube 7 from the plasma spray powder feeder 5 . The outer circumference of this molten metal reservoir 15 ↓ Komo high frequency melting furnace 1
6 is removed, and the molten state of the alloy base material 1 is maintained.

The alloy matrix 1 containing the second phase particles 4 in this way is
The roll 12 is supplied from the lower nozzle of the molten metal reservoir 15 by an inert gas (argon gas) high-pressure device (not shown).
．． It is supplied as a thin uniform continuous jet to the joint of x2, and as in the production example above, it is super cold. I had a prostitute+
1 Bon 4 people 2 Koane No. 13 is obtained f.

This core 13 is also shown in FIG. 3, and the PI is made up of three-dimensionally uniform molecules of fine second phase particles 4 spread across the ultra-quenched metal matrix 14. In addition, in this production line? ! Although the r, ■-r method was used, it is also possible to apply the single roll method instead.

When making an ingot of the alloy motherboard (, () constituting the ultra-quenched alloy 71~ricks, or when remelting the ingot 1- for ultra-quenching, do not use the injection dispersion method as in the previous example). The second phase particles are placed in the molten alloy matrix 42!
11, stirred by high frequency, and then ultra-quenched to three-dimensionally disperse the second phase particles in Alloy 71-Riggs. There are restrictions on the types of lulls and the lulls that can be dispersed. In particular, when the second phase crystal is a totally bent oxide such as Cr, CeO, etc., it has poor wettability with melts of iron, cobal) and nickel, and is extremely difficult to disperse. Moreover, it tends to be unevenly distributed in the surface layer of the ultra-quenched alloy matrix.

The interfacial phenomenon that occurs when second phase particles are added to and dispersed in the alloy base material in a molten state can be considered in the following two stages. That is, in the first step, the second phase particles come into contact with the molten alloy base material, and at this time, the liquid phase of the molten alloy base material, the solid phase of the second phase particles, and argon gas (inert gas) It is a three-phase gas-phase system. The second stage is a stage in which the second phase particles are suspended in the molten alloy matrix, in which case the liquid phase of the molten alloy matrix and the second
It is a two-phase system of in-phase particles.

Furthermore, the three-phase interfacial phenomena described above can be roughly divided into three types: adhesion wetting, expansion wetting, and immersion wetting. The work when adhesion wetting occurs is W a + the work when extended wetting occurs Ws +
Letting the amount of work when immersion wetting occurs be Wl, it is defined as follows.

Wa−γ5v−ySL+γLν −(])W s =γ
sv-γ81--γc, v-(2) Wj=γ5V-γ
SL - (3) In the formula, γSL: Solid phase-liquid interfacial tension γsL: Solid phase interfacial tension γLv: Liquid phase interfacial tension At the gas-solid and liquid-solid interfaces, the surface of the same phase is Since it is considered that there is almost no deformation, the following equation (4) holds true if the contact angle with the liquid phase is θ.

γsv−γSL−γL V 0 cos O−(4) Substituting this into the above equations (1), (2), and (3), respectively, yields the following equations.

Wa= γ L (cos θ + ] -(5)
Ws= 7 L (cosθ-1) =-(6)Wi=
y L V - cos θ - (7) When W is positive in the equation of Fuku et al., J occurs and wettability occurs. The above formula (5) ~
As is clear from (7), in the first stage when the second phase particles come into contact with the molten alloy base material, the contact angle of the second phase particles with respect to the alloy base material, which is 0, has a large influence on the wettability. ing. Metal oxides generally have a large contact angle of 0 with respect to molten metals such as iron, cobalt, and nickel, and therefore have poor wettability.

Therefore, the second phase particles are made into a molten alloy fli material! 11
, and stirred under high frequency, the so-called alloy base material and the second phase particles are not compatible with each other, and the second phase particles tend to be unevenly distributed on the surface M side of the alloy base material. Because of this, the second
When metal oxides are used as phase particles, the amount that can be dispersed in the alloy base material is at most fJ, about 1% by volume, and the amount of dispersion is extremely small, and the effect of adding the second phase particles is fully exerted. Can not.

In this regard, as mentioned above, when making an ingot of the alloy base material or when melting the ingot for ultra-rapid cooling, the injection dispersion method is used to transfer the second phase particles into the molten base metal base material. If a method of adding the second phase particles is adopted, the second phase particles will be mechanically injected into the alloy matrix by strong injection energy.

Therefore, even second phase particles with poor wettability to the alloy base material can be forcibly and uniformly dispersed, making it possible to
There is a margin in the type of phase particles and the amount that can be dispersed, which greatly contributes to improving the properties and functions of the core material.

An example of the contact angle of the solid phase with respect to the metal melt is shown in Table 1 below.

As is clear from Table 2, metal oxides are
In general, the contact angle is larger than that of gold-containing metals, and the wettability is poor compared to that of gold-containing metals.

Next, examples of the present invention will be described.

Example 1 (Co= o5Fea5slx qBx o)ri q
,q(IiC)a,! If(CO7o5Fe4.gS
i:i 5B1o)! + 9 ('JC) 1 (Co=
o qFea 5sii 5 Bx O):I n (
IdC)2(Co=o,5FeJ5si15B10)
−1−, (tic)F(Co=o, sF+3.+,
55i1S[]10)! c, ('jlC)11,)
Create a core (I) consisting of a second-phase particle-dispersed super-quenched alloy with the above composition formula. %
The second phase particle composition is shown in the composition formula ().

The numbers at the bottom right of both parentheses represent the volume % of each f. A similar display method was adopted for the other '3 ¥ examples.

Next, the specific creation procedure will be explained. First, in order to obtain the composition of a desired ultra-quenched alloy, constituent metal Co is added.

Fe, Si, +3 to Co 420.9g, Fe
22.5g, 5i42.7g, and Bflog are weighed, respectively, and melted together in a vacuum high-frequency melting furnace 2 (see Fig. 2) to obtain a molten alloy base material 1.

This alloy base material 1 is poured into a mold 3 as it is.

On the other hand, WC@ powder (second phase particles 4) is filled in advance in a powder feeder 5 for plasma spraying, and is injected toward the mold injection flow of the alloy base material J by high pressure argon gas from a cylinder 6. hru. Note that the injection amount of the WC fine powder is adjusted by the powder feeder 5 so that the volume % of the alloy base material 1 is expressed by the above-mentioned compositional formula. The temperature of the alloy base material J when it is injected into the mold 3 is kept at a temperature that maintains its molten state and does not melt the WC fine powder, which is the second phase particles, that is, about 1
The temperature is adjusted to 200°C.

The WC fine powder that is forcibly injected toward the mold injection flow of the molten alloy base material 1 does not form particles in the alloy base material, but is dispersed in a finely divided state, and the distance between the particles is small. is short.

In this way, the WC fine powder dispersed in a fine state without becoming coarse has a slow floating speed in the alloy base material 1, so that it may segregate when the alloy base material 1 solidifies in the mold 3. The dispersion state is stable. For this reason, Co-Fe-5i with uniformly dispersed WC powder
An ingot 8 made of a -B alloy is obtained.

Next, this ingot 8 is placed in a heat-resistant tube 7 made of quartz glass as shown in FIG.
dissolve. At this time as well, the temperature is maintained at a level at which the WCI# powder does not dissolve, that is, about 1200°C. Next, the piston 11 is actuated to bring the lower end nozzle of the heat-resistant tube 7 as close as possible to the joint between the two rollers 12 and 12 that are rotating at high speed, and the argon gas pressure inside the heat-resistant tube 7 is rapidly increased to Roll 1 with -8 as a uniform continuous jet from the nozzle.
2.12 joints are supplied. Since the rolls 12 and 12 rotate at high speed while being cooled and are constantly pressed against each other, the ejected alloy base material is instantaneously cooled and solidified to a width of 40 mII+ and a thickness of 30 μm.

A ribbon-shaped core material 13 having a length of 5 m is obtained.

When the surface and the cut surface in the thickness direction of this core material 13 were observed with a scanning electron microscope, it was found that the fine WC powder was aggregated with each other at short intervals in the ultra-quenched alloy matrix and became coarse. They are uniformly dispersed individually as fine particles without any pores. This confirmed that the wc powder was uniformly dispersed three-dimensionally in the alloy matrix. Furthermore, it was confirmed by X-ray diffraction that this ultra-quenched alloy matrix kettle was amorphous.

This core piece 13 is continuously punched into a predetermined shape, a predetermined number of sheets are laminated as shown in FIG. 6 and FIG.
and 18a, +8b are created. This 17a, +7))
Lead m: 17. +8a and 18b are the right-side cores, and a coil 19 is wound around each of these cores 17.7a and 18a (see FIG. 6).
18 Beam section main body 20 and lie 1-・
The cross feed shield plates 22 are inserted directly into the respective grooves of the section main body 21, and each cross feed shield plate 22 is also placed at a predetermined neck position, and the assembled whole is housed in the shield case 23 (FIG. 7). The assembly is completed.

Example 2 (Ni= e Six o B 12 ) 9 +,
(wc) - + (N, 8 S1□.B□ 2)
9 2 (WC) 9 (Nj7aSi1oB]: riez(
WC) 19 A core material made of a second phase particle-dispersed ultra-quenched alloy having the above composition formula is prepared.

Next, the specific creation procedure will be explained. First, the constituent metal Ni to obtain the desired composition of the ultra-quenched alloy.

Si and B are each weighed to give 459 g of Ni, 28 g of Sj, and 13 g of B, and these are melted in a vacuum high-frequency melting furnace to create an alloy base material, which is poured into a mold.

WC fine powder (second phase particles) is injected from a plasma spray powder feeder together with high-pressure argon gas into the injection flow of the alloy base material 1, and then cooled and Ni-8j- with the WC fine powder uniformly dispersed. An ink bottle 1- made of a B-based alloy is made. If the temperature of the alloy base material is adjusted to approximately 1200°C when spraying and dispersing the WC fine powder, the added WC fine powder will not dissolve in the alloy base material and will be uniformly dispersed as fine particles. Ru.

The ingot is placed in a heat-resistant tube placed directly above one roll, and the inside of the tube is sufficiently replaced with argon gas. Then, a high frequency melting furnace installed around the outer circumference of the heat-resistant tube melts the
The alloy is heated and maintained at 00°C, and only the alloy base material is remelted.

Thereafter, the argon gas pressure inside the heat-resistant tube is rapidly increased, and the molten alloy mother 44 containing fine WC powder is ejected from the lower nozzle of the heat-resistant tube onto a roll rotating at 2000 r, p, m.

When ejected, it instantly cools and solidifies to a width of 40mm.

A ribbon-shaped core material with a thickness of 30 iim and a length of 5 m is obtained.

When the surface and the cut surface in the thickness direction of this core material were observed with a scanning electron microscope, it was found that WC
The fine powder is uniformly dispersed as fine particles in the ultra-quenched alloy matrix. In addition, this super-quenched alloy matrix
It was confirmed by X-ray diffraction that it was amorphous.

The procedure for manufacturing a magnetic head as shown in FIG. 7 using this core material is the same as that in the previous embodiment, and therefore a description thereof will be omitted.

Example 3 (CO7o, *Fea, zSix sBlo) g9.9
(Crz(h)ol(Coy o5Fea, 5si
15B]O)9 z7(Crz(L+)o,i(Co
−, o, 5Fe−, qSilsBlo)q +115(
Cr=Oa ) o, +; (Co= o qFea 5
sii 5B1 0)G 9 (Crz Ow)1(
Co=o, 5Fe=+ 55ii 5Bio) −+=
(CrzOi)3 A magnetic head is assembled in the same manner as in the previous example using a core material made of a second phase particle dispersed ultra-quenched alloy having the above compositional formula.

Example 4 (Co=o-, Fed, 1Sjz sB>O)9
D9 (CaO2). , (Co-, o5Fea Ss]
1 sel o) Riri 7 (CeC1z)o, :+(
Co= o, s FeJ, q Sjl +, R10)G
9S(Ce0= ) o, 5(Co= o s Fe4
5 Sjl-, Bkoo)! ] 9 (CaO2)
1 (Co= o, iFe, +, 5sj1 zBl 0)
9 = (Ce02)a A magnetic head is assembled in the same manner as in the previous example using a core material made of a second phase particle dispersed ultra-quenched alloy having the above compositional formula.

Example 5 (Co=o, 5Fe45sji!; B) O) 9
9.0 (WO:+)o 1(Co-, o 5Fea
, 5six iBz O)ri9.7 (WO:I)0.
:1 (Co= o 5Fe-+5Sii iBi O)
! 9 r, (WOi)o 5(CO7o, 5Fea
5si1 sBl 0)+19 (Vi'○yo)yu(
Co= o 5Fe4 gsjl zBt O)9 =
A magnetic head is assembled in the same manner as in the previous example using a core material made of a second-phase particle-dispersed ultra-quenched alloy having a bipedal composition formula (WO 3).

Example 6 (Co = o, s Fe-+, s Six s 81
o)99.9 (ZrOz)ol(CO7o,sF
e, +55ii 51h O)94.7 (Zl-0,
! L-I Vl(Co+0.*Faa3sxx 1B
10)! q,i (ZrO:)o=.

(Co-, o5Fe4.; Si1 sBi O)! +
9 (ZrO, -, b(CO7o 5Fea 5Sil
q口xo )9 = (ZrO:: )? A magnetic spatula 1 is assembled in the same manner as in the previous example, using a core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula.

Example 7 (Co = o, s Fe, +, q 5j1-, Blo
)q 9.9 (Y,=○))01(Co= o 5F
e, +, z Sj] s B:l o )-Iku (
Y: Oco) o, ++ (Co= O5FGJ-, si
□, 5B]O)9*, 5(YZ Oi). 5(Co
= o, 5Fe4 zsil 581 0) 09 (Y
zO:I)x(Co=o5Fe-1qsi15B1
o) er7 (YZ0:l)3 A magnetic head is assembled in the same manner as in the previous example using a core material made of a second phase particle dispersed ultra-quenched alloy having the above compositional formula.

Example 8 (Ni= e 5i1o BlZ )90 (ThO=
)J,)<1'Ji=e Siko o Bi:
:)qo(ThO=)z.

A magnetic head is assembled in the same manner as in the previous embodiment using a core material made of a 24+1 particle dispersed ultra-quenched alloy having the above compositional formula.

Example 9 (Ni=s Sir o B ko, G )-1i (
Ti(T:)z(Ni-, 5Sj 3 o B l s
)9 o (TjC)].

A magnetic head is assembled in the same manner as in the previous embodiment using a core material made of a second-phase particle-dispersed ultra-quenched alloy having the above compositional formula.

Furthermore, scanning electron microscopy revealed that TiC was Ni-5
It is uniformly dispersed three-dimensionally in the i-B series ultra-quenched alloy 71-ricks, has no pores, and its alloy matrix is
It was confirmed by line diffraction that it was amorphous.

Example 10 (4 oq CII+ to Fei++, +) 3 a (Nb
C) z(Fe:l'i, 4 Moa C1,a)=l
s (NbC,)S(Fe3 g4 Moq C),
, ) wa o (NbC)1.

Magnetic ΔT 1- is assembled in the same manner as in the previous embodiment using a core material made of a second-phase particle-dispersed ultra-quenched alloy having the above compositional formula. Note that scanning electron microscopy reveals that NbC is Fe-
A non-equilibrium γ-austenite 1~single phase that is uniformly dispersed three-dimensionally in the Mo-C based ultra-rapidly solidified alloy 71, has no pores, and has an ultrafine grain structure in the alloy matrix according to X-ray diffraction. It was confirmed that Since this non-equilibrium γ-austenite 1~ phase is a crystalline alloy, it has higher thermal stability than an amorphous alloy.

Example 11 (Cut, o Zra o )9 o (SiC)+
0(Cue o Zrj o )-, o (SiC)
i.

A magnetic head is assembled in the same manner as in the previous embodiment using a core made of a second-phase particle-dispersed ultra-quenched alloy having the above compositional formula.

Furthermore, scanning electron microscopy revealed that SiC is Cu-Z
It was three-dimensionally uniformly dispersed in the r-based ultra-quenched alloy matrix, with no pores, and it was confirmed by X-ray diffraction that the alloy matrix was amorphous.

Example 12 (Nj7ha Size: ri, 3° (BN)
x.

(Ni= a Sii o Blz)s o(BN)z
.

A magnetic head is assembled in the same manner as in the previous embodiment using a core material made of a bipedal composition type second phase particle dispersed ultra-quenched alloy. Furthermore, by scanning electron microscopy observation, B N ′h<
Ni-Si-B super-quenched alloy matrix 3
It was three-dimensionally uniformly dispersed, had many pores, and it was confirmed by X-ray diffraction that the alloy matrix was amorphous.

Example 13 (Zra s Nba o 5i1s)a o (N
bN)z.

A magnetic head is assembled in the same manner as in the previous embodiment using a core material made of a second-phase particle-dispersed ultra-quenched alloy having the above compositional formula.

Note that scanning electron microscopy revealed that NbN is Zr-N
It was three-dimensionally uniformly dispersed in the b-5i-based ultra-quenched alloy 71-Rix, with no pores, and it was confirmed by X-ray diffraction that the alloy matrix was amorphous.

Example 14 (Co = o, s Fea, s Six r, B 10
)9] (G)+(Co-, oSFe45Six5
BcoO)9! =(C)5(Co-o,, Fe,+,s
Sxx s B x o )! +. ((1:)1.,
,.

A magnetic head is assembled in the same manner as in the previous embodiment using a core made of a second-phase particle-dispersed ultra-quenched alloy having the above compositional formula.

Furthermore, by scanning electron microscopy observation, C7! lICo-
It was confirmed by X-ray diffraction that the Fe-3i-B super-quenched alloy 71 was uniformly dispersed three-dimensionally in the helix without any pores, and that the alloy matrix was amorphous.

Example 15 (Fe cI z B x e ) Wa 9 (Fe)
1 (Feo 2 B x e > G O (Fe) z A magnetic head is assembled in the same manner as in the previous example using a core material made of a second phase particle force dispersion type ultra-quenched alloy having the above compositional formula 6. Electron microscopic observation confirmed that Fe was three-dimensionally uniform and dispersed in the Fe-B-based ultra-quenched alloy 71~x, and X-ray diffraction confirmed that the alloy matrix was an amorphous invar alloy.

Figure 8 is a particle size distribution diagram of the 241st particle in the ultra-quenched alloy matrix, where (a) is T 1C + (b)
is WC, the same figure (c) 1 is CrzOi, the same figure (d) is Z
Fe2 was used as the second phase particle, and CO70sF eJ, 5 S 11-, B
The particles were dispersed in a 10-series ultra-quenched alloy matrix, and the particle size was measured using an electron microscope. The average particle size of each of these second phase particles was approximately 0.0 (i7zm) for A1.As is clear from these figures, approximately 70% or more of the dispersed second phase particles Particle size is approximately 0.1
In order to disperse the second phase particles in the form of ultrafine particles, it is necessary to appropriately adjust the particle size of the second phase particles before addition and the conditions for spraying them.

The following Table 2 shows the ultra-quenched alloy matrix (Co7o, s Fe4.s Sii s B x o
) is a table showing the average particle diameters of other second phase particles in FIG.

Table 2 If most of the second phase particles are M3w particles as described above, the state of dispersion of the second phase particles is stable even in the molten alloy base material. That is, at the stage where the second phase particles are suspended in the molten alloy base material, a dispersion system exists in which the alloy base material is the dispersion medium and the second phase particles are the dispersoid. Since this dispersion system is thermodynamically unstable, the free energy change ΔF is largely involved in the dispersion or aggregation of the second phase particles. Generally, the free energy change ΔF includes a change in interfacial free energy and a change due to a chemical reaction. By the way, when the alloy base material in the molten state and the second phase particles are in an equilibrium state, the free energy change due to the chemical reaction is considered to be the atmosphere, so the dispersion state of the second phase particles is determined by the change in the interfacial free energy. It will be controlled.

The dispersion of the second phase particles in the molten alloy matrix eliminates the solid phase (second phase particles)-solid phase (second phase particles) interface, and the solid phase (second phase particles) and liquid phase (molten alloy This is a change in which an interface (matrix) is formed. Therefore, the change in interfacial free energy at this time, Fs, is defined as shown in the following equation (8). Note that γss in the formula is the interfacial tension at the solid phase-solid phase interface.

ΔFs=2γSL−γss−(8) According to this equation, if the value of ΔFs is negative, the second phase particles will be dispersed or naturally turbid in the i6 alloy base material5, and if it is positive, they will aggregate. F
In order to make s negative, it is necessary to make the particle size of the second phase particles as small as possible, and as mentioned above, about 70% or more of the dispersed second phase particles, preferably is 90
';t to j, -1:'.

If the particle size of Noshino is less than about 0.1)1 m, the second
The particles do not aggregate with each other, and their dispersion state is stable and uniformly dispersed.

Obtained according to Example 1 (Co=o, s Fca, s Siy G Bto
)p ヮ (W C:),! 2+ Magnetic spatula 1~ using A and Pernloy (20%Fe-80%Ni)
) The magnetic permeability of the magnetic head after molding with epoxy resin was 4000 for the former, while the magnetic permeability for the latter was about 800 at most. In the case of the magnetic material according to the present invention, there is hardly any decrease in magnetic permeability due to resin molding, and the magnetic material has high magnetic permeability even after molding. Furthermore, when we measured the peak shift of the signal waveform in the high frequency region, we found that the latter magnetic head using permalloy had a shift amount of 150 to 260 ns, whereas the present invention In the former magnetic head, the shift J'1lO
It is as short as 0 to 150 ns, and the symmetry of the signal waveform in the high frequency region is improved compared to the conventional one. The test conditions for this peak shift were a tape running speed of 125 ip.
s, linear density 9042 F ci , pattern N RZ
I 11,100 (peak shift 1- between 10), write current l5ATX1. It is I3.

The present invention has the above-mentioned configuration, and has high magnetic permeability in the high frequency range and good peak shift symmetry, which reduces the error margin of peripheral devices that use the magnetic head and improves reliability. Improve your skills.

[Brief explanation of the drawing]

1 and 2 are principle explanatory diagrams showing a first manufacturing example of the core material according to the present invention, FIG. 3 is an enlarged sectional view of the manufactured core material, and FIG. 4 is a core material according to the present invention. 5 is a principle explanatory diagram showing a second manufacturing example of the core material according to the present invention. FIG. 6 is a principle explanatory diagram showing a third manufacturing example of the core material according to the present invention.
A partially exploded perspective view of the digital magnetic head according to 5. Figure 7 is a perspective view of the magnetic head of -E- after assembly, Part 8 (a), 0)), (c) . (d) is a particle size distribution diagram of fiS2.1 grains in the alloy 71 helix. 1 Base metal base material, 4 Second phase particles, 12:1A (A, 1
4 Super-quenched alloy matrix 217 core for REET,
+ 8 ・ Core for light. Figure 1 Figure 2 Figure 3 ] 4 Figure 4 Figure 5 Procedural amendment (method) February 10, 1980 Kazuo Wakasugi, Commissioner of the Japan Patent Office ■ Case indication patent application No. 179401 No. 2 Title of the invention Digital magnetic head 3 Relationship to the case of the person making the amendment Applicant address 1-7 Yukitani Otsuka-cho, Ota-ku, Tokyo Name (A
O9) Alps Electric Co., Ltd. Representative Katsutabe Kataoka 4 Agent address 6 Aiya Building, 1-6-13 Nishi-Shinbashi, Minato-ku, Tokyo 105 Subject of amendment (1) Brief explanation of drawings in the specification Column 7 Contents of amendment As stated in the attached sheet (1) Page 36 of the specification, lines 3 to 4 [Figure 8...
・(d) is corrected to [Figure 8 is j, ・“ ・
21-1゛i Agent Patent Attorney 2 Kenji Department

Claims (1)

[Scope of Claims] (1) A super-rapidly solidified alloy 71-ricks consisting of an amorphous, crystalline or mixed phase thereof contains at least b second phase particles.
1. A digital magnetic head, characterized in that at least a part of a magnetic circuit is made of a composite material made of one type of three-dimensionally uniform composite material. (2) The digital magnetic head according to claim (1), wherein the ultra-quenched alloy matrix is a cobalt-based amorphous alloy containing cobalt as a main component. (3) The digital magnetic head according to claim (1), wherein the ultra-quenched alloy matrix is a nickel-based amorphous alloy containing nickel as a main component. (4) A special 6e raw material characterized in that the ultra-quenched alloy 71~Rix is an iron-based amorphous alloy containing iron as a main component.
bma'cm+#/l)mf+aM,;>;Jr+l+
rnO)404,.7(5) The digital magnetic head according to claim 1, wherein the second phase particles are carbide. (6) A digital magnetic head according to claim (5), wherein the second phase particles are tungsten carbide. (7) The digital magnetic head according to claim (1), wherein the second IIJ particles are carbon. (8) The digital magnetic head according to claim (1), wherein the second phase particles are oxides. (9) The digital magnetic head according to claim (8), wherein the second phase particles are chromium oxide. (10) The digital magnetic head according to claim jl) (1), wherein the second phase particles are nitride. (11) A digital magnetic head according to claim (1), wherein the second phase particles are silica 1-. (12) The digital magnetic head according to claim (1), wherein the second phase particles are metal. (13) A patent characterized in that about 70% or more of the second phase particles uniformly dispersed in the ultra-quenched alloy matrix have a particle size of less than about 0.1 μm. A digital magnetic head according to claim (1). (14) The digital magnet according to claim (1), wherein the composite material is made of thin plate members, and the core portion is constituted by a laminate in which a predetermined number of these thin plate members are laminated. head. (15) In the composite material, after the alloy base material constituting the ultra-quenched alloy matrix is heated and melted, and before the alloy base material solidifies, the second phase particles are heated and melted together with an injection medium consisting of an inert gas. The alloy is sprayed and dispersed into the alloy base material, and then cooled to create an ingot in which the second phase particles and particles are uniformly dispersed.This ingot is then remelted to an extent that the second phase particles do not dissolve and solidified by ultra-rapid cooling. A digital magnetic head according to claim 1, characterized in that the digital magnetic head is a bonding material made of (1G) The composite +A mixture heats and melts the alloy base material constituting the ultra-quenched alloy matrix to such an extent that the second phase particles do not dissolve, and before the alloy base material solidifies, the alloy base material made of an inert gas Claim 1, characterized in that the composite material is obtained by spraying and dispersing second phase particles onto the base metal base material using a spraying medium, and then solidifying the composite material by ultra-rapid cooling. Magnetic head for digital. (17) The digital device according to claim (15) or (1G), wherein the second phase particles are a metal that has poor wettability with respect to the ultra-quenched alloy 71-lix. magnetic head. (18) A digital magnetic head according to claim (17), characterized in that the second phase particles are chromium oxide. (19) Uniform molecules 1 in the super-quenched alloy 71 helix.
Claim (15) or (16), characterized in that the particle size of about 70% or more of the second phase particles obtained in the above-mentioned second phase particles is less than about 0.1 μm. The listed digital magnetic head